CN1114711C - Refractory Fe-base alloy - Google Patents
Refractory Fe-base alloy Download PDFInfo
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- CN1114711C CN1114711C CN00109561A CN00109561A CN1114711C CN 1114711 C CN1114711 C CN 1114711C CN 00109561 A CN00109561 A CN 00109561A CN 00109561 A CN00109561 A CN 00109561A CN 1114711 C CN1114711 C CN 1114711C
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 63
- 239000000956 alloy Substances 0.000 title claims abstract description 63
- 239000002245 particle Substances 0.000 claims abstract description 22
- 239000006104 solid solution Substances 0.000 claims abstract description 16
- 238000000034 method Methods 0.000 claims abstract description 8
- 230000003647 oxidation Effects 0.000 claims abstract description 8
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 8
- 238000005728 strengthening Methods 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 32
- 239000011651 chromium Substances 0.000 claims description 15
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- 229910052742 iron Inorganic materials 0.000 claims description 13
- 239000004411 aluminium Substances 0.000 claims description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 10
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 239000000243 solution Substances 0.000 claims description 6
- 239000011159 matrix material Substances 0.000 claims description 5
- 238000001556 precipitation Methods 0.000 claims description 5
- 238000007670 refining Methods 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract description 47
- 230000007797 corrosion Effects 0.000 abstract description 14
- 238000005260 corrosion Methods 0.000 abstract description 14
- 230000008901 benefit Effects 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 2
- 230000002349 favourable effect Effects 0.000 abstract 4
- 230000003078 antioxidant effect Effects 0.000 description 14
- 239000010959 steel Substances 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 5
- 229910000753 refractory alloy Inorganic materials 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 239000003963 antioxidant agent Substances 0.000 description 4
- 235000006708 antioxidants Nutrition 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 230000001590 oxidative effect Effects 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 239000010935 stainless steel Substances 0.000 description 4
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 3
- 238000009415 formwork Methods 0.000 description 3
- 239000000446 fuel Substances 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 229910017604 nitric acid Inorganic materials 0.000 description 3
- 229910000601 superalloy Inorganic materials 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 2
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 2
- 230000033228 biological regulation Effects 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000002485 combustion reaction Methods 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 239000002912 waste gas Substances 0.000 description 2
- 230000004580 weight loss Effects 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 244000035744 Hura crepitans Species 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical compound [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- KCZFLPPCFOHPNI-UHFFFAOYSA-N alumane;iron Chemical compound [AlH3].[Fe] KCZFLPPCFOHPNI-UHFFFAOYSA-N 0.000 description 1
- -1 aluminium chromium carbon Chemical compound 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
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- 238000011065 in-situ storage Methods 0.000 description 1
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- 229910001234 light alloy Inorganic materials 0.000 description 1
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Abstract
The present invention relates to light type iron-base alloy with heat and corrosion resistance and a manufacturing method thereof. The alloy has proper tensile ductility at room temperature, favorable oxidation resistance at high temperature and favorable tensile ductility at high temperature. The present invention also provides a material and a method for strengthening the material; the material is prepared from body centred cubic solid solutions; the method comprises the following steps: the other body centred cubic solid solution particle with the fundamentally same lattice constants as a base is precipitated and extracted in the base of the body centred cubic solid solutions. The alloy has the advantages of convenient processing, favorable mechanical properties and favorable mechanical properties at high temperature; therefore, the alloy can be applied to high-temperature structures, such as components of turbine boosters.
Description
Technical field
What the present invention relates to is a kind of ferrous alloy, and particularly a kind of refractory Fe-base alloy belongs to metal material field.
Background technology
At present, the most frequently used material is above-mentioned nickeliferous high temperature steel, refractory alloy and superalloy on heat resistant structure.Yet,, impel people to seek a kind of more low-gravity heat-stable material that has because this class high temperature steel, refractory alloy and superalloy have than higher proportion.Pottery that is being studied and ordered intermetallic compound have lower proportion, are expected to become the traditional heat-resistance stainless steel of present use and the equivalent material of alloy.Regrettably, they all fail to possess suitable stretching plastic simultaneously, high strength and good antioxidant property, and these over-all propertieies just the high temperature engineering use desired.Because pottery does not have stretching plastic fully, can't bring into play its low-gravity advantage.In addition, ceramic component generally is prepared from by expensive powder sintering process.Because ceramic component lacks plasticity and costs an arm and a leg, so can only be used limitedly.The low-gravity ordered intermetallic compound also fails to obtain suitable room temperature tensile plasticity, and the room temperature fracture toughness is also lower.In addition, prepare this class material and be processed into the Technology that parts also will adopt more complicated, thereby improved productive expense widely.Add that lower temperature-room type plasticity causes the damage of the transmission and the course of processing easily, thereby cause high component processing scrap rate.An example of ordered intermetallic compound is Fe
3Al.Pure iron is the sosoloid of body-centered cubic (BCC) structure, has very high plasticity.Different with pure iron, Fe
3Al is made of orderly body-centered cubic (BCC) structure (generally to form DO in room temperature
3Ordered structure, and form B at high temperature
2Ordered structure).In this ordered structure, Fe and Al atom are arranged at the arrangement of making rule on the fixed position.Fe
3Al has lower proportion, owing to contain higher aluminium content, so have good antioxidant property below 800 ℃.At Fe
3Aluminium in the Al material forms one deck oxide skin easily on the surface in oxidizing atmosphere, though this layer oxide skin and not really firm, and when being higher than 800 ℃ easy peeling.In addition, Fe
3The starting material of Al are more cheap.But Fe
3Al is very crisp, and room temperature tension plasticity is also low, is easier to take place along crystalline substance and transgranular fracture.Though at Fe
3Chromatize improves its tension plasticity limitedly among the Al, and proportion is also lighter, and its density is 6.5g/cm greatly
3, but orderly Fe-Al-Cr composition commonly used but has relatively poor hot strength, resistance to corrosion and resistance of oxidation.Seek a kind of price so keep punching in this field high and have low-gravity, certain plasticity, and the excellent antioxidant property and the heat-stable material of excellent processability are the targets that people pursue.What need especially is a kind of new ferrous alloy, and this alloy should have low-gravity, high strength, suitable stretching plastic and higher anti-oxidant and corrosion resistance nature.
Summary of the invention
The objective of the invention is to overcome deficiency of the prior art, a kind of refractory Fe-base alloy is provided, it is anti-oxidant, corrosion-resistant that it is had, excellent properties such as castability and high strength, and have low-gravity and good stretching plastic.The present invention is achieved by the following technical solutions, and main purpose of the present invention provides the new iron aluminium solid solution alloy with body-centered cubic structure, is specially Fe-Al-Cr-C and constitutes a class material.The objective of the invention is to adopt parts or the matrix material of conventional Technology preparation by the phase composite of Fe-Al-Cr-C sosoloid, and each all is a BCC sosoloid mutually in the matrix material, the lattice constant of each phase is basic identical, and forms good structure matching.Another object of the present invention is to adopt alloy production of the present invention to go out intensifier component, particularly turbine and compressor.
The present invention mainly is about the iron aluminium sosoloid by body-centered cubic structure, is specially the class material that Fe-Al-Cr-C constitutes.This material preferably contains following composition, 10-80 atom % iron, and 10-45 atom % aluminium, 1-70 atom % chromium and 0.9-15 atom % carbon, wherein the total amount of Al and Cr must not be less than 30 atom %.Being converted to weight percent is: 12.3-87.0% iron, 5.3-29.0% aluminium, 1.2-78.3% chromium and 0.2-3.9% carbon.This material has excellent performance, and this material obtains to strengthen by well-known method, comprises solution strengthening, grain refining reinforcement, mutually particle reinforced etc.This material also precipitates in the sosoloid separates out with the essentially identical BCC solid-solution particles of its lattice parameter strengthened (precipitation strength).
Material of the present invention until 1150 ℃ all have excellent resistance of oxidation, and until 650 ℃ all can keep excellent mechanical propertys.
The present invention comprises the solid solution alloy of the new Fe-Al-Cr-C body-centered cubic structure of a class, and this class alloy has low-gravity (at 5.5g/cm
3～7.5g/cm
3Between, be preferably 6.1g/cm
3), suitable room temperature tensile plasticity, excellent hot strength, resistance of oxidation and corrosion resistance nature.
The optimum composition of the alloy of being invented is a 10-80 atom % iron, 10-45 atom % aluminium, and 1-70 atom % chromium and 0.9-15 atom % carbon, wherein the total amount of Al and Cr must not be less than 30 atom %.According to final performance demands, change Cr content and be divided into several Cr content ranges.For example, the scope of cast material is 5-20 atom %Cr, and shape-changing material (forging) then is suitable for lower Cr content, for example, and 1 atom %～10 atom %.In the present invention, determine that by the relative intensity at powder x-ray diffraction peak this material is to be made of mutually BCC.In the present invention, BCC is defined as mutually by single BCC phase or several BCC phase composite with essentially identical lattice parameter.Occur＜3% non-BCC phase time at BCC in mutually and still be defined as the BCC phase, that is exactly that the intensity at the non-BCC peak that occurs in BCC phase X-ray diffraction peak still is defined as the BCC phase less than 3% o'clock of BCC diffraction peak.This regulation is just just used during BCC phase border in determining Fig. 1, and only occurs the BCC diffraction peak in the border, and non-BCC diffraction peak do not occur.Material of the present invention during from room temperature to 650 ℃ yield strength all be higher than 320MPa, and not only do not raise from room temperature to 600 ℃ scope intensity and to descend with temperature, raise on the contrary or remain unchanged.For some composition,, sharply raise with the rising of temperature from room temperature to 600 ℃ YIELD STRENGTH.This phenomenon is different with conventional BCC material, and the BCC YIELD STRENGTH generally raises with temperature and reduces.
This alloy continues to strengthen with following method:
(a) introduce another sosoloid phase;
(b) grain refining;
(c) introduce strengthening phase particle or in sosoloid, add the solid solution strengthened alloy element.
Separate out another BCC solid-solution particles by precipitation in original BCC sosoloid and strengthen, the lattice parameter of two sosoloid is consistent as far as possible.By adding the particle reinforced BCC solid solution matrix of refractory oxide, for example add Y
2O
3Particle.Add a certain amount of Cr and C element, the iron-aluminium alloy of the light proportion sosoloid that is unordered BCC structure from orderly BCC structural transformation.The solid solubility of carbon in material of the present invention increases along with the reduction of the increase of chromium content and aluminium content.
This gently has quite suitable room temperature tensile plasticity than heavy alloy.See that in performance introduction subsequently the combination of low-gravity, suitable stretching plastic and high hot strength is the developing major technological breakthrough of light proportion heat resistant structure material.Conventional Technology (as casting) is used for preparing the parts of different shape easily.
Material of the present invention has excellent antioxidant property, at high temperature is exposed to the antioxidant property quality that changes in weight under the oxidizing atmosphere is defined as material with material.The antioxidant property of material of the present invention is better than stainless steel, high temperature steel, refractory alloy and the superalloy of use at present.Specifically, the rate of weight loss that exposes after 100 hours in 1000 ℃ of air of this material has only 0.2g/m
2My god, be sure of that excellent antioxidant property is owing to contain a large amount of aluminium and chromium element in the material.If desired, also in material, add rare earth element, with further its antioxidant property that improves.
The parts that are prepared into by material composition of the present invention have high hot strength, for example, up to 650 ℃, are higher than the stainless steel of present use, the hot strength of most of high temperature steel and refractory alloy.For example, material of the present invention is under as cast condition, and its 320MPa yield strength remains to 650 ℃ always.This alloy strength is strengthened (for example by the recrystallization annealing after the hot rolling, with the microstructure of change object) by reinforcement approach commonly used as grain refining, and solution strengthening (for example the reinforced alloys element is gone in solid solution in sosoloid) is mutually particle reinforced etc. with second.
Second is mutually particle reinforced by outside adding refractory oxide, as Y
2O
3Better way is mutually particle reinforced by inner in-situ techniques generation second.For example, facilitate from the sosoloid internal precipitate by the composition of adjusting Fe-Al-Cr-C going out the second phase enhanced particles, this particle is still the BCC structure, and their lattice parameter is mated fine with sosoloid.In setting the composition scope, control the quantity and the distribution of body-centered cubic structure particle by the content of adjusting Fe-Al-Cr-C, these particles also have the BCC structure, their lattice parameter and solid solution matrix basically identical, manifest and well join, thereby eliminated the stress that produce owing to two-phase lattice parameter difference on the phase interface, guaranteed the stability of high temperature phase (or microstructure).
Owing to have excellent antioxidant property and high hot strength over-all properties, material of the present invention can come into operation immediately, promptly can be used for the load component that in up to 650 ℃ of following oxidizing atmospheres, turns round, also can be used for the no-load member of being on active service up in 1200 ℃ of following oxidizing atmospheres.
The object of being made by material of the present invention also has good corrosion resistance in salpeter solution.This material at room temperature, the anticorrosive rate in the 20%-65% salpeter solution is the weight loss rate of 0.01mm/.During with in accordance with regulations the condition test of this material, also find no the sign of intergranular corrosion.
Material of the present invention has suitable room temperature tensile plasticity, has good high temperature (being higher than 700 ℃) stretching plastic, so have good hot workability.For example, its room temperature tensile unit elongation greater than about 5%, 900 ℃ stretch percentage elongation greater than 95%.So material of the present invention is easy to by hot rolling being higher than under 900 ℃.
Because material of the present invention has excellent castability, for example, its melt has low viscosity and high flowability, so can be easy to prepare the end form finished product cast with conventional casting technology.Object for example under rare gas element or vacuum, carries out melting by conventional induction furnace under controlled or protective atmosphere.
The present invention has had substantive distinguishing features and marked improvement, and the Master Cost of alloy ratio iron nickel base alloy of the present invention is lower, than traditional nickeliferous steel grade, want light 20-25% and cheap 20-80% as stainless steel, high temperature steel and refractory alloy, this alloy ratio iron nickel base alloy or nickel-base alloy charger turbine are more anti-oxidant.
Description of drawings
Fig. 1 is a frame ternary phase diagrams
Embodiment
As shown in Figure 1, show the phase region of BCC, further provide embodiment below in conjunction with accompanying drawing:
One object is made by conventional smelting technique, and its composition is within scope shown in Figure 1.Under vacuum, make alloy melt by the starting material that this composition is made into, and pour into and have in the object shape die cavity formwork, under vacuum, solidify.This foundry goods that has solidified continues to be cooled to room temperature and forms an as cast condition object in sandbox and in the air.Take out this as cast condition object then from formwork, and find that it is the body-centered cubic sosoloid of Fe-Al-Cr-C, its proportion is 6.1g/cm
3The mechanical property of as cast condition object is listed in table 1, and antioxidant property is listed in table 2, and corrosion resistance nature is listed in table 3.As shown in table 1, material of the present invention has excellent yield strength and tensile strength until 650 ℃, has good plasticity, particularly under 900 ℃.As shown in table 2, material one of the present invention nearly all is oxidation resistant fully until 1150 ℃.As shown in table 3, material of the present invention has excellent corrosion resistance nature, is included in the corrosion resistance nature in 65% nitric acid.
The mechanical property of table 1 Fe-Al-Cr-C body centred cubic alloy
The anti-oxidant voltinism energy of table 2Fe-Al-Cr-C body centred cubic alloy
As shown in table 2, material one of the present invention nearly all is oxidation resistant fully until 1150 ℃.
| Temperature (℃) | 0.2% yield strength σ y (MPa) | Tensile strength sigma b (MPa) | Stretch percentage elongation (%) |
| Room temperature | 360 | 500 | 5.3 |
| 200 | 375 | 580 | 5.8 |
| 400 | 364 | 617 | 8.8 |
| 500 | 353 | 600 | 8.7 |
| 600 | 361 | 530 | 8.7 |
| 650 | 324 | 403 | 9.3 |
| 700 | 170 | 247 | 33 |
| 750 | 116 | 168 | 43 |
| 800 | 90 | 112 | 66.7 |
| 900 | 54 | 68 | 95.8 |
| 1000 | 26 | 32 | 39.2 |
| Temperature (℃) | Expose the weight rate (g/m after 100 hours in the air 2/ day) |
| ?600 | ?0.015 |
| ?700 | ?0.074 |
| ?800 | ?0.065 |
| ?900 | ?0.096 |
| ?1000 | ?-0.2 |
| ?1100 | ?-2 |
| ?1150 | ?0.42 |
The corrosion resistance nature of table 3Fe-Al-Cr-C body centred cubic alloy
| Concentration of nitric acid (%) | Corrosion rate (mm/) |
| 5 | 0.04 |
| 20 | 0.009 |
| 35 | 0.0084 |
| 80 | 0.0064 |
| 65 | 0.0075 |
As shown in table 3, material of the present invention has excellent corrosion resistance nature, is included in the corrosion resistance nature in 65% nitric acid.
When concrete the application, cast out the object that minimum wall thickness (MINI W.) is 0.5mm with the vacuum fusible pattern foundry engieering.Shown in following sample, this is the foundry goods of the turbine of a supercharging blower, and it has the excellent hot strength up to 650 ℃.The hot strength of the iron Refractoloy that adopts to present supercharging blower is similar.Yet, because material of the present invention has lower proportion (6.1g/cm
3), with the iron nickel-base casting alloy (8.1g/cm of present employing
3) compare, reducing by 25%, therefore its specific tenacity exceeds 25%.High specific tenacity and low proportion can make the charger turbine of being made by material of the present invention lighter at least more than 25% than cast iron casting base alloy charger turbine.
Light charger turbine is easier to overcome inertia, reaches running speed quickly, reduces the pick-up period, pollutes thereby reduce moment.Because this effect, the pick-up period shortens more than 25%, causes the efficiency of combustion of supercharging blower of the heavier iron-nickel alloy of boost phase higher.In fact, charger turbine and the compressor made with light alloy of the present invention will help diesel engine except satisfying stable state waste gas release standard, can also satisfy moment the waste gas release standard of (acceleration) attitude.
The present invention is easy to be cast as nearly end form (no surplus) object.The ability of this uniqueness is because the result that the characteristic of the flowability of alloy melt and strengthening phase combines.In fact, this cast material is an eutectic structure.This tissue bond excellent flowability guarantees that alloy melt is filled into each corner of foundry goods formwork, thereby casts out the object of nearly end form (no surplus) that this object need not last precision work and can use.
The present invention can be applied to the high performance diesel supercharging blower of boats and ships, truck and car immediately.Because diesel engine has better fuel economy than petrol motor, so be widely adopted.In high-speed diesel engine, adopt supercharging blower to improve fuel economy greatly, improve the efficient of diesel engine and reduce pollution.Most of in the world industrial truck and 10% car (reaching 20% in Europe, is 10% in Japan) use the high-speed diesel engine that has supercharging blower.A diesel pressure booster is made up of compressor and turbine.Consider that from mechanical kinetic energy turbine is the parts of most critical,,, bear the high centrifugal stress that produces owing to high speed rotating, and in oxidation and corrosive environment, turn round as up to 650 ℃ because it at high temperature turns round.At present, charger turbine adopts the Ni-based or nickel-base alloy of iron to cast, and is not only expensive but also very heavy.Because the inertia that weight produces, turbine needs the regular hour to remove to overcome this inertia before the rotating speed that reaches the most effective running, so weight is heavy more, the inertia that need overcome is big more, and the needed pick-up period is big more.Clear proof is exactly that the tail gas with black smoke can appear in truck when quickening suddenly, and this tail gas is that the interior fuel of the pick-up period section before turbine reaches required rotating speed does not have perfect combustion to cause.Solve above-mentioned Fe-Ni base and the Ni base is made the problem that charging turbine and compressor bring by made charger turbine of the iron aluminium chromium carbon alloy of indication of the present invention and compressor.
Claims (19)
1, a kind of refractory Fe-base alloy, it is characterized in that, constitute by Fe-Al-Cr-C body-centered cubic sosoloid, its atomic percent scope is: 10-80 atom % iron, 10-45 atom % aluminium, 1-70 atom % chromium and 0.9-15 atom % carbon are converted to weight percent and are: 12.3-87.0% iron, 5.3-29.0% aluminium, 1.2-78.3% chromium and 0.2-3.9% carbon.
2, this refractory Fe-base alloy according to claim 1 is characterized in that alloy is a polycrystal.
3, this refractory Fe-base alloy according to claim 1 is characterized in that the total amount of Al+Cr is at least 30 atom %.
4, this refractory Fe-base alloy according to claim 1, it is characterized in that yield strength with room temperature to 650 ℃ all greater than 320MPa.
5, this refractory Fe-base alloy according to claim 1 is characterized in that being strengthened by following method:
A, in original sosoloid, introduce another sosoloid;
B, grain refining;
The particle that c, introducing are made of a kind of strengthening phase perhaps adds a solution strengthening element in sosoloid.
6, this refractory Fe-base alloy according to claim 5 is characterized in that alloy precipitation in the primary solid solution is separated out with the essentially identical body-centered cubic solid-solution particles of its lattice parameter to be strengthened.
7, this according to claim 1 or 5 refractory Fe-base alloy is characterized in that alloy is by adding the refractory oxide particle, to strengthen original sosoloid.
8, this according to claim 1 or 5 refractory Fe-base alloy is characterized in that alloy refractory oxide particle is Y
2O
3
9, this refractory Fe-base alloy according to claim 1, the proportion that it is characterized in that alloy are 5.5 to 7.5g/cm
3
10, this refractory Fe-base alloy according to claim 9, the proportion that it is characterized in that alloy is 6.1g/cm
3
11, this refractory Fe-base alloy according to claim 1, the yield strength that it is characterized in that alloy ℃ remain unchanged or rise with temperature from room temperature to 600 to be increased.
12, this refractory Fe-base alloy according to claim 1 is characterized in that alloy at temperature height to 1150 ℃, does not produce changes in weight because of oxidation basically.
13, this refractory Fe-base alloy according to claim 1, it is characterized in that alloy at 900 ℃ stretching plastic greater than 95%.
14, this refractory Fe-base alloy according to claim 1 is characterized in that Fe-Al-Cr-C body-centered cubic sosoloid composition matrix material, and each sosoloid all is the body-centered cubic single phase solid solution, and these sosoloid have essentially identical lattice constant.
15, this refractory Fe-base alloy according to claim 2 is characterized in that described polycrystalline Fe-Al-Cr-C sosoloid, and the total amount of its Al+Cr is at least 30 atom %.
16, this refractory Fe-base alloy according to claim 2 is characterized in that described polycrystalline Fe-Al-Cr-C sosoloid, separates out another body-centered cubic solid-solution particles by precipitation and strengthens.
17, this refractory Fe-base alloy according to claim 2, it is characterized in that described polycrystalline Fe-Al-Cr-C sosoloid, separate out another body-centered cubic solid-solution particles by precipitation and strengthened, this particle has and the essentially identical lattice constant of protocorm sosoloid.
18, this refractory Fe-base alloy according to claim 2 is characterized in that described polycrystalline Fe-Al-Cr-C sosoloid, and the refractory oxide particle that is added into is strengthened.
19, this refractory Fe-base alloy according to claim 2 is characterized in that described polycrystalline Fe-Al-Cr-C sosoloid, and refractory oxide is Y
2O
3
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US09/540,403 US6524405B1 (en) | 2000-02-11 | 2000-03-31 | Iron base high temperature alloy |
| US09/540,403 | 2000-03-31 |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 02148353 Division CN1250759C (en) | 2002-03-31 | 2000-07-04 | Heat-resistant corrosion resistant iron base alloy |
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| Publication Number | Publication Date |
|---|---|
| CN1315586A CN1315586A (en) | 2001-10-03 |
| CN1114711C true CN1114711C (en) | 2003-07-16 |
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| CN00109561A Expired - Fee Related CN1114711C (en) | 2000-03-31 | 2000-07-04 | Refractory Fe-base alloy |
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|---|---|---|---|---|
| US10557464B2 (en) | 2015-12-23 | 2020-02-11 | Emerson Climate Technologies, Inc. | Lattice-cored additive manufactured compressor components with fluid delivery features |
| US10982672B2 (en) * | 2015-12-23 | 2021-04-20 | Emerson Climate Technologies, Inc. | High-strength light-weight lattice-cored additive manufactured compressor components |
| US10634143B2 (en) | 2015-12-23 | 2020-04-28 | Emerson Climate Technologies, Inc. | Thermal and sound optimized lattice-cored additive manufactured compressor components |
| CN109986074A (en) * | 2019-03-08 | 2019-07-09 | 北京矿冶科技集团有限公司 | Fe3Al/Cr7C3Powder and preparation method thereof and respective coatings |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4769214A (en) * | 1985-09-19 | 1988-09-06 | Sptek | Ultrahigh carbon steels containing aluminum |
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2000
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Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4769214A (en) * | 1985-09-19 | 1988-09-06 | Sptek | Ultrahigh carbon steels containing aluminum |
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| CN1315586A (en) | 2001-10-03 |
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